CN114427052B - Ni 3 Al-based alloy and additive manufacturing method thereof - Google Patents

Ni 3 Al-based alloy and additive manufacturing method thereof Download PDF

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CN114427052B
CN114427052B CN202210093751.7A CN202210093751A CN114427052B CN 114427052 B CN114427052 B CN 114427052B CN 202210093751 A CN202210093751 A CN 202210093751A CN 114427052 B CN114427052 B CN 114427052B
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based alloy
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powder
selective laser
additive manufacturing
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CN114427052A (en
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任忠鸣
王江
陈超越
刘明宇
帅三三
胡涛
徐松哲
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University of Shanghai for Science and Technology
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University of Shanghai for Science and Technology
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C19/00—Alloys based on nickel or cobalt
    • C22C19/03—Alloys based on nickel or cobalt based on nickel
    • C22C19/05—Alloys based on nickel or cobalt based on nickel with chromium
    • C22C19/051—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W
    • C22C19/057—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W with the maximum Cr content being less 10%
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F10/00—Additive manufacturing of workpieces or articles from metallic powder
    • B22F10/20—Direct sintering or melting
    • B22F10/28—Powder bed fusion, e.g. selective laser melting [SLM] or electron beam melting [EBM]
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B33—ADDITIVE MANUFACTURING TECHNOLOGY
    • B33Y—ADDITIVE MANUFACTURING, i.e. MANUFACTURING OF THREE-DIMENSIONAL [3-D] OBJECTS BY ADDITIVE DEPOSITION, ADDITIVE AGGLOMERATION OR ADDITIVE LAYERING, e.g. BY 3-D PRINTING, STEREOLITHOGRAPHY OR SELECTIVE LASER SINTERING
    • B33Y10/00—Processes of additive manufacturing
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B33—ADDITIVE MANUFACTURING TECHNOLOGY
    • B33Y—ADDITIVE MANUFACTURING, i.e. MANUFACTURING OF THREE-DIMENSIONAL [3-D] OBJECTS BY ADDITIVE DEPOSITION, ADDITIVE AGGLOMERATION OR ADDITIVE LAYERING, e.g. BY 3-D PRINTING, STEREOLITHOGRAPHY OR SELECTIVE LASER SINTERING
    • B33Y80/00—Products made by additive manufacturing
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C1/00—Making non-ferrous alloys
    • C22C1/04—Making non-ferrous alloys by powder metallurgy
    • C22C1/0433—Nickel- or cobalt-based alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C19/00—Alloys based on nickel or cobalt
    • C22C19/007—Alloys based on nickel or cobalt with a light metal (alkali metal Li, Na, K, Rb, Cs; earth alkali metal Be, Mg, Ca, Sr, Ba, Al Ga, Ge, Ti) or B, Si, Zr, Hf, Sc, Y, lanthanides, actinides, as the next major constituent
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
    • Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
    • Y02P10/00—Technologies related to metal processing
    • Y02P10/25—Process efficiency

Abstract

The invention belongs to Ni 3 The technical field of Al-based alloy, the invention relates to pre-alloyed Ni 3 Al powder is added into the Al powder to improve the Al content in the alloy, thereby introducing beta-NiAl phase and improving gamma' -Ni 3 Toughness of Al phase, making Ni 3 The phase composition and the structure appearance of the Al-based alloy are changed, the number of cracks is reduced, high-temperature mechanical property is shown, and the Ni is further improved by controlling the laser power of selective laser melting 3 High temperature mechanical properties of the Al-based alloy. The results of the examples show that Ni prepared by the method provided by the present invention 3 The Al-based alloy had a tensile strength at 650 ℃ of 927.1MPa, an elongation at break at 650 ℃ of 4.4%, a tensile strength at 1000 ℃ of 193.5MPa, and an elongation at break at 1000 ℃ of 47.5%.

Description

Ni 3 Al-based alloy and additive manufacturing method thereof
Technical Field
The invention relates to Ni 3 Al-based alloy technical field, in particular to Ni 3 An Al-based alloy and a method for additive manufacturing thereof.
Background
In comparison with the conventional subtractive manufacturing method by reducing a plurality of parts, which is based on a layer-by-layer incremental manufacturing method, most of the additive manufacturing techniques generally use powder or wire as a raw material, are melted by a concentrated heat source, and are solidified during a subsequent cooling process to form a part, which has been receiving attention in the past decades because of its high degree of freedom in design and low process cycle.
Selective laser melting is one of additive manufacturing, and selective laser melting mainly utilizes laser to perform single-point scanning along a planned path, powder is spread layer by layer, and the powder is overlapped layer by layer, so that net forming of a metal structure is realized. In selective laser melting, the next layer has remelting action on the upper layer, so that the homogenization of defects is facilitated, and the defects such as segregation, pores, impurities and the like are less formed in each layer. In addition, selective laser melting has high melt solidification speed, is beneficial to the development of fine grains, and obtains extremely high supersaturation degree, thereby preparing parts with high mechanical properties.
Ni-Al intermetallic compounds are widely considered to be a new generation of aeroengine blade material hopeful to replace the traditional nickel-based high-temperature alloy due to excellent mechanical properties, and through decades of development, various Ni-based intermetallic compounds are developed 3 Al is used as a matrix, and B, zr, hf, cr and other elements are added to strengthen the alloy, so that the alloy has good comprehensive performance and is widely applied to the aviation industry. Ni developed at present 3 Most Al-based alloys have a gamma + gamma' two-phase structure, have the advantages of high specific strength, excellent oxidation resistance, low crack propagation rate and the like, and have poor high-temperature mechanical properties. Therefore, how to prepare Ni with excellent high-temperature mechanical properties by selective laser melting 3 Al-based alloys have become a problem in the art that needs to be solved.
Disclosure of Invention
The object of the present invention is to provide a Ni 3 Al-based alloy and additive manufacturing method thereof, and Ni prepared by using method provided by the invention 3 The Al-based alloy has excellent high-temperature mechanical properties.
In order to achieve the above purpose, the invention provides the following technical scheme:
the invention provides Ni 3 An additive manufacturing method of an Al-based alloy, comprising: mixing Al powder with prealloyed Ni 3 Mixing Al powder and then carrying out selective laser melting to obtain Ni 3 An Al-based alloy;
said Ni 3 The mass content of Al in the Al-based alloy is 14-15%;
the laser power for selective laser melting is 180-220W.
Preferably, the particle size of the Al powder is 15-53 μm; the prealloyed Ni 3 The grain diameter of the Al powder is 15-53 mu m.
Preferably, the pre-alloyed Ni is in mass percent 3 The Al powder comprises the following components: 80 to 82 percent of Ni, 8 to 9 percent of Al, 7 to 8 percent of Cr, 1.2 to 1.5 percent of Mo, 1.5 to 2.0 percent of Zr and 0.005 to 0.008 percent of B.
Preferably, the Ni is calculated by mass percent 3 The Al-based alloy comprises the following components: 74 to 75 percent of Ni, 14 to 15 percent of Al, 7 to 8 percent of Cr, 1.2 to 1.5 percent of Mo, 1.5 to 2.0 percent of Zr and 0.005 to 0.008 percent of B.
Preferably, the Ni is calculated by mass percentage 3 The Al-based alloy comprises the following components: 74.1% of Ni, 14.7% of Al, 7.7% of Cr, 1.43% of Mo, 1.7% of ZrC, 0.008% of B and the balance of impurities.
Preferably, the scanning speed of selective laser melting is 1000-2600 mm/s.
Preferably, the scanning interval of selective laser melting is 50-100 μm.
Preferably, the thickness of the powder spread melted in the selective laser area is 30-40 μm.
The invention also provides Ni in the technical scheme 3 Ni prepared by additive manufacturing method of Al-based alloy 3 Al-based alloy, said Ni 3 The phase composition of the Al-based alloy comprises gamma' -Ni 3 An Al phase and a beta-NiAl phase.
The invention provides Ni 3 An additive manufacturing method of an Al-based alloy, comprising: mixing Al powder with prealloyed Ni 3 Mixing Al powder and then carrying out selective laser melting to obtain Ni 3 An Al-based alloy; the Ni 3 The mass content of Al in the Al-based alloy is 14-15%; the laser power for selective laser melting is 180-220W. The invention is through pre-alloying Ni 3 Al powder is added into the Al powder to improve the Al content in the alloy, thereby introducing beta-Ni 3 Al phase, and the introduction of beta-NiAl phase can improve gamma' -Ni 3 Toughness of Al phase such that Ni 3 The phase composition and the structure appearance of the Al-based alloy are changed, the number of cracks is reduced, high-temperature mechanical property is shown, and Ni can be enabled by controlling the laser power of selective laser melting 3 The Al-based alloy obtains better surface quality and reduces internal poresAnd generation of cracks, thereby further improving Ni 3 High temperature mechanical properties of the Al-based alloy. The results of the examples show that Ni prepared by the method provided by the present invention 3 The Al-based alloy had a tensile strength at 650 ℃ of 927.1MPa, an elongation at break at 650 ℃ of 4.4%, a tensile strength at 1000 ℃ of 193.5MPa, and an elongation at break at 1000 ℃ of 47.5%.
Drawings
FIG. 1 shows Ni provided by the present invention 3 A process flow diagram of an additive manufacturing method of an Al-based alloy;
FIG. 2 shows pre-alloyed Ni in example 1 of the present invention 3 A morphology map of the Al powder;
FIG. 3 shows Al-Ni enrichment in example 1 of the present invention 3 The shape graph of the Al alloy powder;
FIG. 4 shows Ni prepared in comparative example 1 3 Microstructure of Al alloy;
FIG. 5 shows Ni prepared in example 1 of the present invention 3 Microstructure diagram of Al-based alloy.
Detailed Description
The invention provides Ni 3 An additive manufacturing method of an Al-based alloy, comprising: mixing Al powder with prealloyed Ni 3 Mixing Al powder and then carrying out selective laser melting to obtain Ni 3 An Al-based alloy;
the mass content of Al in the Ni3 Al-based alloy is 14-15%;
the laser power for selective laser melting is 180-220W.
The invention mixes Al powder with prealloyed Ni 3 Mixing Al powder and then carrying out selective laser melting to obtain Ni 3 An Al-based alloy. The invention is through pre-alloying Ni 3 Al powder is added into the Al powder to improve the Al content in the alloy, so that a beta-NiAl phase is introduced to improve the high-temperature mechanical property of the alloy, and the laser selective melting process is combined to further improve Ni 3 High temperature mechanical properties of the Al-based alloy.
The Al powder and the prealloyed Ni are preferably mixed in the invention 3 The Al powders are respectively dried and then mixed. In the invention, the drying temperature is preferably 120-150 ℃; said driedThe time is preferably 8 to 10 hours; the equipment used for drying is preferably a constant-temperature vacuum drying oven. The invention preferably removes the moisture in the powder by drying, prevents the influence of moisture absorption on the forming quality of the alloy and improves the fluidity of the powder in the powder laying process.
In the present invention, the Al powder is preferably pure Al powder. In the present invention, the particle size of the Al powder is preferably 15 to 53 μm, more preferably 15 to 35 μm; the prealloyed Ni 3 The particle size of the Al powder is preferably 15 to 53 μm, and more preferably 15 to 35 μm. In the present invention, when the Al powder and prealloyed Ni are used 3 When the particle diameter of the Al powder is out of the above range, it is preferable in the present invention to mix the Al powder with pre-alloyed Ni 3 And mixing and ball-milling the Al powder. The operation of the powder mixing and ball milling is not particularly limited, and the two kinds of powder can be fully mixed to obtain mixed powder with the particle size of 15-53 mu m and uniform and spherical powder particles. In the present invention, the method of mixing the powders is preferably a mechanical mixing method; the equipment used for ball milling is preferably a ball mill.
In the present invention, the pre-alloyed Ni is present in mass percent 3 The Al powder preferably includes the following components: 80 to 82 percent of Ni, 8 to 9 percent of Al, 7 to 8 percent of Cr, 1.2 to 1.5 percent of Mo, 1.5 to 2.0 percent of Zr and 0.005 to 0.008 percent of B, more preferably 81.1 percent of Ni, 8 percent of Al, 7.7 percent of Cr, 1.43 percent of Mo, 1.7 percent of Zr, 0.008 percent of B and the balance of impurities.
In the present invention, the Ni 3 The Al content in the Al-based alloy is 14 to 15% by mass, preferably 14.7%. The invention is through pre-alloying Ni 3 Al powder is added into the Al powder to improve the Al content in the alloy, so that a beta-NiAl phase is introduced to improve the high-temperature mechanical property of the alloy.
In the present invention, the Ni is present in mass percent 3 The Al-based alloy preferably includes the following components: 74 to 75 percent of Ni, 14 to 15 percent of Al, 7 to 8 percent of Cr, 1.2 to 1.5 percent of Mo, 1.5 to 2.0 percent of Zr and 0.005 to 0.008 percent of B, more preferably 74.1 percent of Ni, 14.7 percent of Al, 7.7 percent of Cr, 1.43 percent of Mo, 1.7 percent of Zr, 0.008 percent of B and the balance of impurities.
After the mixing is finished, the invention willThe mixed powder is subjected to selective laser melting to obtain Ni 3 An Al-based alloy. The invention adopts the selective laser melting method to prepare Ni 3 The Al-based alloy is beneficial to reducing segregation and improving the high-temperature mechanical property of the alloy, and the material utilization rate is high.
In the invention, the laser power for selective laser melting is 180-220W, preferably 180-200W. The invention can control the laser power of selective laser melting to enable Ni 3 The Al-based alloy obtains better surface quality, reduces the generation of pores and cracks in the alloy and is beneficial to obtaining Ni with better high-temperature mechanical property 3 An Al-based alloy.
In the present invention, the scanning speed for selective laser melting is preferably 1000 to 2600mm/s, more preferably 1100 to 1800mm/s, and most preferably 1100 to 1300mm/s. The invention is beneficial to reducing the generation of pores and cracks in the alloy by controlling the scanning speed of selective laser melting, thereby obtaining Ni with better high-temperature mechanical property 3 An Al-based alloy.
In the present invention, the scanning pitch for selective laser melting is preferably 50 to 100 μm, and more preferably 75 to 100 μm. The invention preferably controls the scanning distance of selective laser melting in the range, which is favorable for ensuring Ni 3 High temperature mechanical properties of the Al-based alloy.
In the invention, the thickness of the powder spread for selective laser melting is preferably 30-40 μm, and more preferably 30-35 μm. The invention preferably controls the powder laying thickness of the selective laser melting in the range, which is beneficial to ensuring Ni 3 High temperature mechanical properties of the Al-based alloy.
In the invention, the substrate used for selective laser melting is preferably a hastelloy substrate. The invention preferably polishes the substrate prior to selective laser melting. The invention preferably removes oxides and stains on the surface of the substrate by polishing, thereby being more beneficial to obtaining Ni with excellent high-temperature mechanical property 3 An Al-based alloy. In the present invention, the material for the sanding is preferably sandpaper.
In the present invention, the apparatus used for selective laser melting is preferably a ProX2003D printer.
In the present invention, the scanning strategy of selective laser melting is preferably a hexagonal scanning strategy.
Ni provided by the invention 3 The process flow diagram of the additive manufacturing method of the Al-based alloy is shown in figure 1, and Al powder and prealloyed Ni are mixed 3 Al powder is placed in a powder cylinder of a ProX2003D printer, laser is used as an energy source, layer-by-layer scanning is carried out on a metal powder bed layer according to a path planned in a three-dimensional CAD slice model under a vacuum environment, and the scanned Al-Ni-rich powder 3 The Al alloy powder achieves the effect of metallurgical bonding through melting and solidification, and finally Ni is obtained 3 An Al-based alloy.
The invention is through pre-alloying Ni 3 Al powder is added into the Al powder to improve the Al content in the alloy and introduce a beta-NiAl phase, and the introduction of the beta-NiAl phase can improve gamma' -Ni 3 Toughness of Al phase, making Ni 3 The phase composition and the structure appearance of the Al-based alloy are changed, the number of cracks is reduced, high-temperature mechanical property is shown, and Ni can be enabled to be molten by controlling the laser power of selective laser melting 3 The Al-based alloy has better surface quality, and reduces the generation of internal pores and cracks, thereby further improving the high-temperature mechanical property of the alloy.
The invention also provides Ni in the technical scheme 3 Ni prepared by additive manufacturing method of Al-based alloy 3 Al-based alloy, said Ni 3 The phase composition of the Al-based alloy includes gamma' -Ni 3 An Al phase and a beta-NiAl phase. In the present invention, the γ' -Ni 3 Al phase and beta-NiAl phase form a composite structure, so that Ni 3 The high-temperature mechanical property of the Al-based alloy is obviously improved.
In the present invention, the β -NiAl phase is preferably in a particle distribution; the Ni 3 The Al phase is preferably a single crystal.
The technical solution of the present invention will be clearly and completely described below with reference to the embodiments of the present invention. It is to be understood that the described embodiments are merely exemplary of the invention, and not restrictive of the full scope of the invention. All other embodiments, which can be derived by a person skilled in the art from the embodiments given herein without making any creative effort, shall fall within the protection scope of the present invention.
Example 1
Pre-alloyed Ni 3 Respectively placing Al powder and pure Al powder in a constant-temperature vacuum drying oven, drying at 120 deg.C for 8 hr, and pre-alloying Ni after drying 3 Mixing Al powder and pure Al powder by a mechanical mixing method, and ball-milling by a ball mill to obtain Al-Ni-rich powder with excellent sphericity and a powder particle size range of 15-53 mu m 3 Al alloy powder; wherein pre-alloyed Ni 3 The chemical composition of the Al powder is as follows (mass content): 81.1% of Ni, 8% of Al, 7.7% of Cr7, 1.43% of Mo, 1.7% of ZrC, 0.008% of B and the balance of impurities;
will be rich in Al-Ni 3 Placing Al alloy powder in a ProX2003D printer for selective laser melting, adopting a Hastelloy substrate, polishing the surface of the substrate with sand paper to be bright, setting the laser power for selective laser melting to be 180W, the scanning speed to be 1100mm/s, the scanning interval to be 75 mu m, the layer thickness to be 30 mu m, and the scanning strategy to be a hexagon strategy to obtain Ni 3 The Al-based alloy comprises the following chemical components in percentage by mass: 74.1 percent of Ni, 14.7 percent of Al, 7.7 percent of Cr, 1.43 percent of Mo, 1.7 percent of ZrC, 0.008 percent of B and the balance of impurities, ni 3 The Al-based alloy has no defect on the surface, the density of the formed part is up to more than 99.9 percent, the alloy structure is uniform, and no component segregation exists.
FIG. 2 shows pre-alloyed Ni in example 1 3 The morphology of Al powder, FIG. 3 is the Al-Ni-rich alloy of example 1 3 And (3) a morphology graph of the Al alloy powder. As can be seen from figures 2 and 3, the sphericity of the two powders is better, the particle size distribution of the powders is uniform, and the requirements of the powders melted in the selective laser area are met.
Example 2
The difference from example 1 is that the laser power is 200W.
Example 3
The difference from example 1 is that the scanning speed is 1300mm/s.
Comparative example 1
The difference from example 1 is that no pure Al powder is added.
Comparative example 2
The difference from example 1 is that the laser power was 250W.
Comparative example 3
The difference from example 1 is that Ni 3 The mass content of Al in the Al-based alloy is 10%.
FIG. 4 shows Ni prepared in comparative example 1 3 Microstructure of Al alloy, FIG. 5 is Ni prepared in example 1 3 Microstructure diagram of Al-based alloy. As can be seen from FIG. 5, ni prepared in example 1 3 The microstructure of Al-base alloy has finer dendritic crystal in single molten pool, ni 3 The Al dendrite is broken into particles and dispersed in Ni 3 On Al substrate, thereby forming NiAl and Ni 3 A novel composite structure consisting of an Al matrix.
The high-temperature mechanical properties of the alloys prepared in examples 1 to 3 and comparative examples 1 to 3 were tested according to GB/T4338-2006 "Metal Material high-temperature tensile test method", the alloys prepared in examples 1 to 3 and comparative examples 1 to 3 were processed into tensile samples of 2mm thickness, each alloy sample was 3, then the samples were subjected to high-temperature tensile property tests at 650 ℃ and 1000 ℃ respectively on an electronic universal tester with a heating furnace, 3 samples were tested under the same conditions and averaged, and the test results are shown in Table 1.
TABLE 1 high temperature tensile Strength and elongation at Break of alloys prepared in examples 1-3 and comparative examples 1-3
Comparative example 1 Comparative example 2 Comparative example 3 Example 1 Example 2 Example 3
Tensile strength at 650 ℃ (MPa) 592.7 605.4 549.9 688 927.1 773.7
Elongation at break at 650 ℃ (%) 3.6 3.8 3.9 4 4.4 6
Tensile Strength (MPa) at 1000 DEG C 118 130 166 178 193.5 143
Elongation at Break at 1000 ℃ (%) 43.5 42.9 42.4 44 47.5 46.25
As can be seen from Table 1, the use of Ni according to the present invention 3 Ni prepared by additive manufacturing method of Al-based alloy 3 The high-temperature tensile strength and the elongation at break of the Al-based alloy are both obviously increased.
As can be seen from the above examples, the present invention provides Ni 3 Ni prepared by additive manufacturing method of Al-based alloy 3 The Al-based alloy has excellent high-temperature mechanical properties, wherein the tensile strength at 650 ℃ is 927.1MPa, the elongation at break at 650 ℃ is 4.4%, the tensile strength at 1000 ℃ is 193.5MPa, and the elongation at break at 1000 ℃ is 47.5%.
The foregoing is only a preferred embodiment of the present invention, and it should be noted that, for those skilled in the art, various modifications and decorations can be made without departing from the principle of the present invention, and these modifications and decorations should also be regarded as the protection scope of the present invention.

Claims (7)

1. Ni 3 The additive manufacturing method of the Al-based alloy specifically comprises the following steps: mixing Al powder with prealloyed Ni 3 Mixing Al powder and then carrying out selective laser melting to obtain Ni 3 An Al-based alloy;
the pre-alloyed Ni is calculated by mass percent 3 The Al powder comprises the following components: 80 to 82 percent of Ni, 8 to 9 percent of Al, 7 to 8 percent of Cr, 1.2 to 1.5 percent of Mo, 1.5 to 2.0 percent of Zr, 0.005 to 0.008 percent of B and the balance of impurities;
by mass percent, the Ni 3 The Al-based alloy comprises the following components: 74 to 75 percent of Ni, 14 to 15 percent of Al, 7 to 8 percent of Cr, 1.2 to 1.5 percent of Mo, 1.5 to 2.0 percent of Zr, 0.005 to 0.008 percent of B and the balance of impurities;
said Ni 3 The phase composition of the Al-based alloy comprises gamma' -Ni 3 An Al phase and a beta-NiAl phase;
the laser power for selective laser melting is 200 to 220W.
2. Ni according to claim 1 3 The additive manufacturing method of the Al-based alloy is characterized in that the grain diameter of the Al powder is 15-53 mu m; the prealloyed Ni 3 The particle size of the Al powder is 15-53 mu m.
3. Ni according to claim 1 3 Method for the additive manufacturing of an Al-based alloy, characterized in that the Ni is, in mass percent, ni 3 The Al-based alloy comprises the following components: 74.1% of Ni, 14.7% of Al, 7.7% of Cr, 1.43% of Mo, 1.7% of ZrC, 0.008% of B and the balance of impurities.
4. Ni according to claim 1 3 The additive manufacturing method of the Al-based alloy is characterized in that the scanning speed of selective laser melting is 1000-2600 mm/s.
5. Ni according to claim 1 3 The additive manufacturing method of the Al-based alloy is characterized in that the scanning interval of selective laser melting is 50-100 mu m.
6. Ni according to claim 1 3 The additive manufacturing method of the Al-based alloy is characterized in that the powder spreading thickness of selective laser melting is 30-40 μm.
7. Ni as defined in any one of claims 1 to 6 3 Ni prepared by additive manufacturing method of Al-based alloy 3 Al-based alloy, said Ni 3 The phase composition of the Al-based alloy includes gamma' -Ni 3 An Al phase and a beta-NiAl phase.
CN202210093751.7A 2022-01-26 2022-01-26 Ni 3 Al-based alloy and additive manufacturing method thereof Active CN114427052B (en)

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